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Oppositely, by addition of 0. Accordingly, the Cd-refined AZ31 alloy exhibits higher tensile and impact toughness and Brinell hardness properties than the Sb- Alloy FE380 one.

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Shabestari, R. In general, small quantities of strontium between to ppm are sufficient to produce a Alloy FE380, fibrous eutectic silicon which in turn significantly improves the mechanical properties and machining characteristics of the aluminum casting. Patent No.


Because strontium metal is very reactive with oxygen, nitrogen and moisture, its use as a modifying agent is limited. In most cases, strontium is added in the form of a master alloy. As reported by John E. Gruzleski Alloy FE380 Bernard M.

Similar results are found in U. In contrast, Alloy FE380. In addition, the customary process used to produce strontium-silicon master alloys results in substantial quantities of detrimental impurities including iron, barium and calcium often being present in the master alloy.

Aluminum-strontium binary alloys are now widely used for modifying aluminum castings; however, it has been difficult Alloy FE380 increase the strontium content of these binary master alloys. This is best explained in the context of the aluminum-strontium binary equilibrium phase diagram of Figure 1. The phase diagram contains two low melting Alloy FE380 eutectics, one at about 3.

Since these intermetallic alloys contain no low melting point, finely divided eutectic phase, they are more brittle and dissolve much more slowly than the eutectic containing alloys. The presence of these high melting point intermetallics alloys has placed a significant limitation on the amount of strontium which can be effectively contained in commercial aluminum-strontium binary master alloys. These compositional relationships are Alloy FE380 valid if the rate of solidification is slow enough to allow the phases to reach compositional equilibrium at every instant.

Alloy FE380 more rapid rate of solidification will lead to quite different compositional results. As the melt temperature continues to decrease during solidification, more and more of this primary Al4Sr intermetallic phase precipitates. The primary Al4Sr intermetallic phase is present as massive interconnected plates or needles which are shown two-dimensionally in the photomicrograph given in Figure 2. As displayed in Fig. Therefore, in Xu et al.

Alloy FE380 Network Driver

However, in contrast to the liquidus and Alloy FE380 temperatures respectively, in order to refining mechanism, the presence of Cu and Mg seems to not calculate more easily the effect of solute elements on grain compromise the Sr-modification of eutectic Si morphology. Intermetallic Compounds Investigations 3. Eutectic Si Characterization It is largely reported that in secondary Al alloys several It has largely known that the eutectic Si represents a crucial intermetallic compounds can form due to the substantial microstructural parameter governing the mechanical proper- ties of Al—Si foundry alloys.

A uniform distribution of fine and fibrous eutectic Si particles contributes positively to the fracture strain, as it makes more difficult for the silicon particles to fracture. The microstructure of eutectic Si can be controlled by addition of certain modifying elements, such as Na, Sr, and by increasing the cooling rate [42]. The average size of the eutectic Si particles, Deq estimated for each alloy at the edge and core regions is shown in Fig. Alloy FE380 least particles were measured for each zone in order to provide a suitable statistical analysis.

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The Deq increases along the solidification path from the casting surface to the central region. Along the die wall the nucleation prevails on growing mechanism, due to higher undercooling. Thus, the formation of fine and fibrous eutectic silicon is promoted. The size of eutectic Si particles in this region is almost similar for all the analysed alloys, suggesting that the resulting refined microstructure is effectively obtained by high solidi- fication rate more than Sr-modification. The change of the eutectic Si size and morphology through variation of chemical composition is more evident at the centre, where higher solidification times occur.

The influence of strontium on the microstructure of gravity cast Al—Si Alloy FE380 is Alloy FE380 reported in literature [17,29,30,42—44].

Although the further addition of Cu and Alloy FE380 causes a slight reduction of the eutectic Si size if compared to the base alloy, the other experimental alloys Alloys B, C and D with the same Sr content of alloy A do not exhibit the same refinement degree. The reason can be attributed to Mg and Cu which may counteract the effect of Sr-modification. However, it seems, from Fig. Similar results were observed by Heusler and Schneider [8] and Joenoes [45] in Mg-free and Mg-containing alloys modified with Sr. Concerning Cu, Heusler and Schneider [8] also observed a coarsening effect of eutectic Si in a modified AlSi9 alloy by increasing the Cu content; this effect suggests Fig.

Fitting curves Alloy FE380. The the latter are a consequence of high fraction of Fe-rich Fig. Mg-rich phases were mainly found in the alloy D where the Mg level was highest 0. In Alloy FE380. A low amount of Ni is attributed to the different numbers of Fe and Mn atoms in was occasionally detected in some Cu-bearing compounds.

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In general, the lower the Fe: Mn ratio, Fig. These results seem to interplanar distance dhkl values from XRD spectrum Alloy FE380 the agree with the work of Wang et al.

Solidification Behavior and Mechanical Properties of Al-Si-Mg Alloy with Ti Addition

Alloy FE380 Alloy Network Drivers. FEZIP (FE NetworkCard Driver File) This site maintains listings of network drivers available on the web, organized by company. Alloy Computer Products, your IP & Networking Communications distributor in the USA. FEZIP, Alloy FE380, SepKB, Sep

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